Effect of tempering temperature on the microstructure and properties of ultrahigh-strength stainless steel

doi:10.1016/j.jmst.2019.01.009

Abstract

Abstract:

The microstructure, precipitation and mechanical properties of Ferrium S53 steel, a secondary hardening ultrahigh-strength stainless steel with 10% Cr developed by QuesTek Innovations LLC, upon tempering were studied by scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD), and tensile and impact tests. Based on these results, the influence of the tempering temperature on the microstructure and properties was discussed. The results show that decomposition occurred when the retained austenite was tempered above 440 °C and that the hardening peak at 482 °C was caused by the joint strengthening of the precipitates and martensite transformation. Due to the high Cr content, the trigonal M₇C₃ carbide precipitated when the steel was tempered at 400 °C, and M₇C₃ and M₂C (5-10 nm in size) coexisted when it was tempered at 482 °C. When the steel was tempered at 630 °C, M₂C and M₂₃C₆ carbides precipitated, and the sizes were greater than 50 nm and 500 nm, respectively, but no M₇C₃ carbide formed. When the tempering temperature was above 540 °C, austenitization and large-size precipitates were the main factors affecting the strength and toughness.

Key words: Age hardening, Austenite, Precipitation, Tempering, Strengthening mechanism, M₇C₃

Yangpeng Zhang, Dongping Zhan, Xiwei Qi, Zhouhua Jiang. Effect of tempering temperature on the microstructure and properties of ultrahigh-strength stainless steel[J]. J. Mater. Sci. Technol., 2019, 35(7): 1240-1249.

Figures/Tables 14

Fig. 1. (a) XRD patterns and (b) austenite contents of different samples.

Fig. 2. Microstructures of different samples: (a) S200; (b) S400; (c) S460; (d) S482; (e) S540; (f) S630.

Fig. 3. (a) Bright field image of austenite, (b) dark field image of austenite and (c) lath martensite morphology of sample SQ.

Fig. 4. Microstructure of sample SC: (a) martensite matrix and diffraction calibration; (b) HRTEM image of martensite and diffraction calibration; (c) short-range order regions.

Fig. 5. Microstructure and precipitates in sample S400: (a) martensite and needle-like M7C3; (b) HRTEM image of M7C3 and diffraction calibration; (c) HRTEM images of small M7C3 carbides; (d, e) FFT and diffraction calibration of the martensite matrix and small M7C3.

Fig. 6. Microstructure of sample S482: (a) lath martensite; (b) martensite twins.

Fig. 7. Carbides in sample S482: (a) carbides in martensite twins; (b) EDP and calibration of M7C3 and M2C carbides; (c) HRTEM image of M7C3; (d) calibration of M7C3.

Fig. 8. Microstructure of sample S630: (a) lath martensite; (b) large-size austenite; (c) bright field image of austenite; (d) dark field image of austenite.

Fig. 9. Mapping results of sample S630 (BF: bright field image).

Table 1 Composition of secondary phases in sample S630.

Position	Fe	Co	Cr	Ni	Mo	W	V
Experimental steel	67	14	10	5.7	2	1	0.3
①	73.65	15.92	6.38	2.62	0.53	0.64	0.25
②	56.90	13.43	14.1	10.05	3.18	1.59	0.45
③	41.71	9.82	32.90	2.30	8.37	18	0.73
④	55.2	12.08	12.34	2.83	12.15	5.89	0.20
⑤	39.23	5.76	39.10	0.96	7.88	6.10	0.98
⑥	49.68	11.14	11.35	2.93	18.10	6.54	0.25

Fig. 10. Carbides in sample S630: (a) M23C6-type carbide; (b) calibration of M23C6; (c) M2C-type carbide; (d) calibration of M2C.

Fig. 11. Mechanical properties of samples: (a) strain-stress curves; (b) TS and YS; (c) elongation and impact toughness.

Fig. 12. Dilatometric curve of Ferrium S53 steel.

Fig. 13. EDS result of the M7C3 carbide in sample S482.

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